CZ305540B6 - Heat treatment process of high-alloy steel - Google Patents
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- CZ305540B6 CZ305540B6 CZ2014-348A CZ2014348A CZ305540B6 CZ 305540 B6 CZ305540 B6 CZ 305540B6 CZ 2014348 A CZ2014348 A CZ 2014348A CZ 305540 B6 CZ305540 B6 CZ 305540B6
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/004—Thixotropic process, i.e. forging at semi-solid state
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Heat Treatment Of Steel (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
Description
Oblast technikyTechnical field
Vynález se týká způsobu tepelného zpracování vysokolegované oceli výsledně tvořené strukturou z nerozpuštěných karbidů kovu v podobě globulitických částic, s austenitickou a martenzitickou strukturou.The invention relates to a process for heat treatment of high-alloy steel resulting from a structure of undissolved metal carbides in the form of globulite particles, with an austenitic and martensitic structure.
Dosavadní stav technikyBACKGROUND OF THE INVENTION
Vysokolegované oceli jsou v literatuře označovány, jako oceli s obsahem legujících prvků je vyšší než 10 %. Kombinací legujících prvků se dosahuje potřebných mechanických, fyzikálních a chemických vlastností. Vlastnosti takových ocelí jsou závislé nejen na chemickém složení, ale především na struktuře - tj. na fázovém složení a na tvaru a uspořádání jednotlivých fází. Požadované struktury se dosahuje u ocelí vhodného chemického složení tepelným zpracováním. Tepelné zpracování zahrnuje všechny postupy, při nichž se vnitřní stavba kovu záměrně mění pomocí změn teploty.High-alloy steels are referred to in the literature as steels with an alloying element content greater than 10%. The combination of alloying elements achieves the necessary mechanical, physical and chemical properties. The properties of such steels depend not only on the chemical composition, but above all on the structure - ie the phase composition and the shape and arrangement of the individual phases. The required structure is achieved in steels of suitable chemical composition by heat treatment. Heat treatment includes all processes in which the internal structure of the metal is intentionally changed by temperature changes.
Při tepelném zpracování mohou probíhat změny struktury ve dvou směrech: je-li struktura v nerovnovážném stavu, lze použít postupů směřujících k dosažení termodynamické rovnováhy, kterou představuje diagram Fe-Fe3C. Tyto postupy se souhrnně označují jako žíhání. Při tomto druhu zpracování vzniká v závislosti na obsahu uhlíku feritická, feriticko-perlitická nebo ledeburitická struktura. Druhou skupinou procesů je vytváření nerovnovážných struktur, které vznikají rychlým ochlazením. Tím vznikají martenzitické a bainitické struktury s vysokou pevností, avšak malou houževnatostí. Tyto procesy se označují jako kalení. Dále je kupříkladu známé tepelné zpracování označované jako tixotropní tváření. Vhodnost ocelí pro tixotropní tváření je dána mnoha kritérii. Nej častěji jsou popisovány technologickými parametry, které dokumentují jejich chování při jejich zpracování v semi-solid stavu. Zpravidla nej sledovanější z nich je teplotní interval mezi solidem a likvidem, neboť dosavadní technika nebyla schopna řídit teplotu v objemu zpracovávaného materiálu s potřebnou přesností a dostatečně malými odchylkami teplot. Čím širší je interval mezi solidem a likvidem, tím rovnoměrnějších vlastností lze v objemu materiálu dosáhnout. Nejčastěji je udáváno, že tento interval závisí zejména na chemickém složení materiálu. Částečně ho lze ovlivnit způsobem ohřevu a jeho rychlostí, ev. i strukturou výchozího materiálu. Informace o korelacích s výchozí strukturou se v literatuře prakticky nevyskytují. Vhodnost ocelí pro zpracování v semi-solid stavu není však dána jen absolutním teplotním intervalem mezi solidem a likvidem, ale zejména křivkou popisující podíl solidu a likvidu v závislosti na teplotě při procesu natavování. Ta však může být značně závislá na struktuře a lokálním přerozdělení chemického složení. Co se týče strukturního stavu a zejména přípravy ocelového polotovaru pro tixotropní tváření jiným než klasickým způsobem, jsou informace v literatuře zatím uvedeny pouze v ojedinělých případech.Heat treatment can undergo structural changes in two directions: if the structure is in an unbalanced state, procedures to achieve the thermodynamic equilibrium represented by the Fe-Fe 3 C diagram can be used. These procedures are collectively referred to as annealing. Depending on the carbon content, this type of treatment produces a ferritic, ferritic-perlitic or ledeburitic structure. The second group of processes is the formation of non-equilibrium structures that are formed by rapid cooling. This creates martensitic and bainitic structures with high strength but low toughness. These processes are referred to as quenching. Furthermore, for example, heat treatment known as thixotropic forming is known. The suitability of steels for thixotropic forming is determined by many criteria. Most often they are described by technological parameters, which document their behavior during their processing in semi-solid state. As a rule, the most watched of them is the temperature interval between solid and liquid, since the prior art has not been able to control the temperature in the volume of the material to be processed with the necessary accuracy and sufficiently small temperature variations. The wider the interval between solid and liquid, the more uniform properties can be achieved in the material volume. Most often it is stated that this interval depends mainly on the chemical composition of the material. It can be partially influenced by the way of heating and its speed, ev. structure of the starting material. Information on correlations with the initial structure is virtually absent in the literature. However, the suitability of steels for semi-solid processing is not only determined by the absolute temperature interval between solid and liquid, but in particular by the curve describing the proportion of solid and liquidus as a function of temperature during the melting process. However, it can be highly dependent on the structure and local redistribution of the chemical composition. As far as the structural state and in particular the preparation of the steel semi-finished product for thixotropic forming in other than classical way, the information in the literature has so far been given only in isolated cases.
Podstata vynálezuSUMMARY OF THE INVENTION
Vynález se týká způsobu tepelného zpracování vysokolegované oceli. Při takovém zpracování vzniká speciální struktura, která je tvořena nerozpuštěnými karbidy kovu v podobě globulitických částic, s austenitickou a martenzitickou strukturou.The invention relates to a method of heat treatment of high-alloy steel. Such a treatment produces a special structure consisting of undissolved metal carbides in the form of globulitic particles with an austenitic and martensitic structure.
Způsob tepelného zpracování vysokolegované oceli je tvořen následujícím postupem: kovový polotovar se ohřeje se na teplotu v rozmezí od 1270 do 1280 °C, rychlostí ohřevu v rozmezí od 40 až 45 °C/s, poté se na kovový polotovar působí tlakem v tixotropním procesu a následně nechá se vychladnout na teplotu okolí.The method of heat treatment of high alloy steel comprises the following method: the metal blank is heated to a temperature in the range of 1270 to 1280 ° C, a heating rate in the range of 40 to 45 ° C / s, then the metal blank is pressurized in a thixotropic it is then allowed to cool to ambient temperature.
- 1 CZ 305540 B6- 1 GB 305540 B6
Objasnění výkresůClarification of drawings
Na obrázku č. 1 a obr. č. 2 je vyobrazena výsledná struktura za použití světelného mikroskopu, na obr. č. 3 je vyobrazena výsledná struktura za použití skenovacího mikroskopu.Figures 1 and 2 show the resulting structure using a light microscope, Figure 3 shows the resultant structure using a scanning microscope.
Příklady uskutečnění vynálezuDETAILED DESCRIPTION OF THE INVENTION
Pro experimentální příklad byla zvolena ocel, které by svým chemickým složením odpovídala a umožňuje navrženou koncepci zpracování. Na základě výpočtů byla vybrána ocel CPM 15 V vyrobená práškovou metalurgií. V základním stavu je tvořena karbidy vanadu a chrómu uloženými ve feritické matrici. Jedná se o ocel s vysokou odolností vůči opotřebení a vysokou tvrdostí. Její velkou nevýhodou je nízká tvařitelnost a obrobitelnost.For the experimental example, steel was chosen which would correspond to its chemical composition and allow the proposed processing concept. CPM 15 V steel made by powder metallurgy was selected on the basis of calculations. In its basic state it consists of vanadium and chromium carbides embedded in a ferritic matrix. It is a steel with high wear resistance and high hardness. Its great disadvantage is its low formability and machinability.
Tab. 1: Chemické složení oceli CPM 15V (% hmotn.)Tab. 1: Chemical composition of CPM 15V steel (wt.%)
Pro získání ucelenějšího obrazu o mechanických vlastnostech byla dále zvolena zkouška tlakem, díky které lze porovnávat deformační odezvu na zatěžování materiálu.In order to obtain a more complete picture of mechanical properties, a compression test was chosen, which allows comparing the deformation response to material loading.
Ve výchozím stavu byla naměřena průměrná hodnota tvrdosti 298 HV10. Ve stavu po tixotropním tváření byla tvrdost 728 HV10. Stejný trend byl pozorován při zkoušce tlakem, kde mez kluzu vzrostla z původní hodnoty 627 na 1990 MPa, což představuje trojnásobný nárůst. Toto výrazné zvýšení pevnosti v tlaku lze přisuzovat zejména vzniku martenzitu v matrici a vyloučení chrómu ve formě síťoví. Mikrostruktura materiálu byla po tixotropním tváření tvořena globulárními karbidy vanadu, uloženými v austenitické matrici, jak je vidět na obr. 1 a obr. 2. Na základě rentgenové difrakční fázové analýzy bylo zjištěno, že struktura oceli CPM 15V po tixotropním tváření ve středu produktu při teplotě 1270 °C byla tvořena směsí austenitu 50%, fází železa s kubickou prostorově centrovanou mřížkou 29% a karbidy vanadu V8C7 21%. V případě fáze železa alfa se jedná o martenzit. Při srovnání s výchozím stavem oceli CPM 15V bylo zjištěno, že karbidy V8C7 zůstaly ve struktuře zachovány a došlo k přeměně feritické matrice na austenit a martenzit. Výskyt těchto karbidů ve struktuře přináší produktům nové možnosti, jako je například vysoká otěruvzdomost. Produkt byl podroben měření tvrdosti dle Vickerse po celé své délce.In the initial state, an average hardness value of 298 HV10 was measured. In the thixotropic forming state, the hardness was 728 HV10. The same trend was observed in the compression test, where the yield strength increased from the original value of 627 to 1990 MPa, which is a threefold increase. This significant increase in compressive strength can be attributed mainly to the formation of martensite in the matrix and the exclusion of chromium in the form of mesh. The microstructure of the material after thixotropic forming was formed by globular vanadium carbides embedded in an austenitic matrix as shown in Fig. 1 and Fig. 2. 1270 ° C consisted of austenite mixture of 50%, iron phase with cubic spatially centered grid of 29% and vanadium carbide V8C7 21%. The iron alpha phase is martensite. In comparison with the initial state of CPM 15V steel, it was found that V8C7 carbides remained in the structure and the ferritic matrix was converted to austenite and martensite. The occurrence of these carbides in the structure brings new possibilities to the products, such as high abrasion resistance. The product was subjected to Vickers hardness measurements over its entire length.
Tab. 2: Srovnání parametrů meze kluzu v tlaku a tvrdosti podle VickerseTab. 2: Comparison of parameters of compressive yield strength and hardness according to Vickers
-2CZ 305540 B6-2GB 305540 B6
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CZ2014-348A CZ2014348A3 (en) | 2014-05-21 | 2014-05-21 | Heat treatment process of high-alloy steel |
US14/716,618 US9765418B2 (en) | 2014-05-21 | 2015-05-19 | Microstructure of high-alloy steel and a heat treatment method of producing the same |
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Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
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CZ306020B6 (en) * | 2015-03-10 | 2016-06-22 | Západočeská Univerzita V Plzni | Process for producing ledeburitic high alloy steel by heat treatment |
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CN110216268B (en) * | 2019-06-21 | 2021-05-18 | 北京科技大学 | High-carbon high-alloy steel semi-solid forming temperature-control cooling heat treatment process |
Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0758023A1 (en) * | 1995-08-08 | 1997-02-12 | The Timken Company | Steel machine component having refined surface microstructure and process for forming the same |
EP1031631A2 (en) * | 1999-02-22 | 2000-08-30 | Ovako Steel AB | A method of spheroidizing annealing of hypo-eutectoid low alloy steel |
WO2005103317A2 (en) * | 2003-11-12 | 2005-11-03 | Northwestern University | Ultratough high-strength weldable plate steel |
US20060137781A1 (en) * | 2004-12-29 | 2006-06-29 | Mmfx Technologies Corporation, A Corporation Of The State Of California | High-strength four-phase steel alloys |
WO2007024192A1 (en) * | 2005-08-24 | 2007-03-01 | Uddeholm Tooling Aktiebolag | Steel alloy and tools or components manufactured out of the steel alloy |
WO2010040333A1 (en) * | 2008-10-08 | 2010-04-15 | Peter Barth | Biocompatible material made of stainless steel having a martensitic surface layer |
CZ2010850A3 (en) * | 2010-11-19 | 2012-05-30 | Západoceská Univerzita V Plzni | Method of thixotropic forming of small parts and apparatus for making the same |
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2014
- 2014-05-21 CZ CZ2014-348A patent/CZ2014348A3/en not_active IP Right Cessation
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- 2015-05-19 US US14/716,618 patent/US9765418B2/en not_active Expired - Fee Related
Patent Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0758023A1 (en) * | 1995-08-08 | 1997-02-12 | The Timken Company | Steel machine component having refined surface microstructure and process for forming the same |
EP1031631A2 (en) * | 1999-02-22 | 2000-08-30 | Ovako Steel AB | A method of spheroidizing annealing of hypo-eutectoid low alloy steel |
WO2005103317A2 (en) * | 2003-11-12 | 2005-11-03 | Northwestern University | Ultratough high-strength weldable plate steel |
US20060137781A1 (en) * | 2004-12-29 | 2006-06-29 | Mmfx Technologies Corporation, A Corporation Of The State Of California | High-strength four-phase steel alloys |
WO2007024192A1 (en) * | 2005-08-24 | 2007-03-01 | Uddeholm Tooling Aktiebolag | Steel alloy and tools or components manufactured out of the steel alloy |
WO2010040333A1 (en) * | 2008-10-08 | 2010-04-15 | Peter Barth | Biocompatible material made of stainless steel having a martensitic surface layer |
CZ2010850A3 (en) * | 2010-11-19 | 2012-05-30 | Západoceská Univerzita V Plzni | Method of thixotropic forming of small parts and apparatus for making the same |
Non-Patent Citations (1)
Title |
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(Dagmar Jandová, Svetelná a elektronová mikroskopie svarového spoje oceli P91; konference Metal 2005, Hradec nad Moravicí; http://www.metal2014.com/files/proceedings/metal_05/papers/190.pdf) 24. az 26.5.2005 * |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CZ306020B6 (en) * | 2015-03-10 | 2016-06-22 | Západočeská Univerzita V Plzni | Process for producing ledeburitic high alloy steel by heat treatment |
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US9765418B2 (en) | 2017-09-19 |
US20150337417A1 (en) | 2015-11-26 |
CZ2014348A3 (en) | 2015-11-25 |
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